WO2013080650A1 - Matériau en alliage d'aluminium et structure en alliage d'aluminium et leur procédé de production - Google Patents

Matériau en alliage d'aluminium et structure en alliage d'aluminium et leur procédé de production Download PDF

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WO2013080650A1
WO2013080650A1 PCT/JP2012/075404 JP2012075404W WO2013080650A1 WO 2013080650 A1 WO2013080650 A1 WO 2013080650A1 JP 2012075404 W JP2012075404 W JP 2012075404W WO 2013080650 A1 WO2013080650 A1 WO 2013080650A1
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Prior art keywords
aluminum alloy
mass
less
alloy material
intermetallic compound
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PCT/JP2012/075404
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English (en)
Japanese (ja)
Inventor
新倉昭男
藤田和子
村瀬崇
大谷良行
黒崎友仁
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古河スカイ株式会社
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Priority to ES12853959.0T priority Critical patent/ES2613590T3/es
Priority to KR1020147018291A priority patent/KR101581607B1/ko
Priority to EP12853959.0A priority patent/EP2787094B1/fr
Priority to CN201280045064.2A priority patent/CN103930577B/zh
Priority to JP2013506400A priority patent/JP5337326B1/ja
Priority to US14/361,740 priority patent/US9574253B2/en
Priority to IN1031MUN2014 priority patent/IN2014MN01031A/en
Priority to BR112014013132-5A priority patent/BR112014013132B1/pt
Publication of WO2013080650A1 publication Critical patent/WO2013080650A1/fr
Priority to US15/411,739 priority patent/US9903008B2/en

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    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C21/00—Alloys based on aluminium
    • C22C21/02—Alloys based on aluminium with silicon as the next major constituent
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B23—MACHINE TOOLS; METAL-WORKING NOT OTHERWISE PROVIDED FOR
    • B23K—SOLDERING OR UNSOLDERING; WELDING; CLADDING OR PLATING BY SOLDERING OR WELDING; CUTTING BY APPLYING HEAT LOCALLY, e.g. FLAME CUTTING; WORKING BY LASER BEAM
    • B23K20/00—Non-electric welding by applying impact or other pressure, with or without the application of heat, e.g. cladding or plating
    • B23K20/14—Preventing or minimising gas access, or using protective gases or vacuum during welding
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B23—MACHINE TOOLS; METAL-WORKING NOT OTHERWISE PROVIDED FOR
    • B23K—SOLDERING OR UNSOLDERING; WELDING; CLADDING OR PLATING BY SOLDERING OR WELDING; CUTTING BY APPLYING HEAT LOCALLY, e.g. FLAME CUTTING; WORKING BY LASER BEAM
    • B23K20/00—Non-electric welding by applying impact or other pressure, with or without the application of heat, e.g. cladding or plating
    • B23K20/22—Non-electric welding by applying impact or other pressure, with or without the application of heat, e.g. cladding or plating taking account of the properties of the materials to be welded
    • B23K20/233—Non-electric welding by applying impact or other pressure, with or without the application of heat, e.g. cladding or plating taking account of the properties of the materials to be welded without ferrous layer
    • B23K20/2333—Non-electric welding by applying impact or other pressure, with or without the application of heat, e.g. cladding or plating taking account of the properties of the materials to be welded without ferrous layer one layer being aluminium, magnesium or beryllium
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B32—LAYERED PRODUCTS
    • B32B—LAYERED PRODUCTS, i.e. PRODUCTS BUILT-UP OF STRATA OF FLAT OR NON-FLAT, e.g. CELLULAR OR HONEYCOMB, FORM
    • B32B15/00—Layered products comprising a layer of metal
    • B32B15/01—Layered products comprising a layer of metal all layers being exclusively metallic
    • B32B15/016—Layered products comprising a layer of metal all layers being exclusively metallic all layers being formed of aluminium or aluminium alloys
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B32—LAYERED PRODUCTS
    • B32B—LAYERED PRODUCTS, i.e. PRODUCTS BUILT-UP OF STRATA OF FLAT OR NON-FLAT, e.g. CELLULAR OR HONEYCOMB, FORM
    • B32B15/00—Layered products comprising a layer of metal
    • B32B15/01—Layered products comprising a layer of metal all layers being exclusively metallic
    • B32B15/017—Layered products comprising a layer of metal all layers being exclusively metallic one layer being formed of aluminium or an aluminium alloy, another layer being formed of an alloy based on a non ferrous metal other than aluminium
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C1/00—Making non-ferrous alloys
    • C22C1/02—Making non-ferrous alloys by melting
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C21/00—Alloys based on aluminium
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C21/00—Alloys based on aluminium
    • C22C21/02—Alloys based on aluminium with silicon as the next major constituent
    • C22C21/04—Modified aluminium-silicon alloys
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C21/00—Alloys based on aluminium
    • C22C21/10—Alloys based on aluminium with zinc as the next major constituent
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C21/00—Alloys based on aluminium
    • C22C21/12—Alloys based on aluminium with copper as the next major constituent
    • C22C21/14—Alloys based on aluminium with copper as the next major constituent with silicon
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C21/00—Alloys based on aluminium
    • C22C21/12—Alloys based on aluminium with copper as the next major constituent
    • C22C21/18—Alloys based on aluminium with copper as the next major constituent with zinc
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22F—CHANGING THE PHYSICAL STRUCTURE OF NON-FERROUS METALS AND NON-FERROUS ALLOYS
    • C22F1/00—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working
    • C22F1/04—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working of aluminium or alloys based thereon
    • C22F1/043—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working of aluminium or alloys based thereon of alloys with silicon as the next major constituent
    • F—MECHANICAL ENGINEERING; LIGHTING; HEATING; WEAPONS; BLASTING
    • F28—HEAT EXCHANGE IN GENERAL
    • F28F—DETAILS OF HEAT-EXCHANGE AND HEAT-TRANSFER APPARATUS, OF GENERAL APPLICATION
    • F28F1/00—Tubular elements; Assemblies of tubular elements
    • F28F1/10—Tubular elements and assemblies thereof with means for increasing heat-transfer area, e.g. with fins, with projections, with recesses
    • F28F1/12—Tubular elements and assemblies thereof with means for increasing heat-transfer area, e.g. with fins, with projections, with recesses the means being only outside the tubular element
    • F28F1/126—Tubular elements and assemblies thereof with means for increasing heat-transfer area, e.g. with fins, with projections, with recesses the means being only outside the tubular element consisting of zig-zag shaped fins
    • F—MECHANICAL ENGINEERING; LIGHTING; HEATING; WEAPONS; BLASTING
    • F28—HEAT EXCHANGE IN GENERAL
    • F28F—DETAILS OF HEAT-EXCHANGE AND HEAT-TRANSFER APPARATUS, OF GENERAL APPLICATION
    • F28F21/00—Constructions of heat-exchange apparatus characterised by the selection of particular materials
    • F28F21/08—Constructions of heat-exchange apparatus characterised by the selection of particular materials of metal
    • F28F21/081—Heat exchange elements made from metals or metal alloys
    • F28F21/084—Heat exchange elements made from metals or metal alloys from aluminium or aluminium alloys
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B23—MACHINE TOOLS; METAL-WORKING NOT OTHERWISE PROVIDED FOR
    • B23K—SOLDERING OR UNSOLDERING; WELDING; CLADDING OR PLATING BY SOLDERING OR WELDING; CUTTING BY APPLYING HEAT LOCALLY, e.g. FLAME CUTTING; WORKING BY LASER BEAM
    • B23K2101/00—Articles made by soldering, welding or cutting
    • B23K2101/04—Tubular or hollow articles
    • B23K2101/14—Heat exchangers
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B23—MACHINE TOOLS; METAL-WORKING NOT OTHERWISE PROVIDED FOR
    • B23K—SOLDERING OR UNSOLDERING; WELDING; CLADDING OR PLATING BY SOLDERING OR WELDING; CUTTING BY APPLYING HEAT LOCALLY, e.g. FLAME CUTTING; WORKING BY LASER BEAM
    • B23K2103/00—Materials to be soldered, welded or cut
    • B23K2103/08—Non-ferrous metals or alloys
    • B23K2103/10—Aluminium or alloys thereof
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22F—CHANGING THE PHYSICAL STRUCTURE OF NON-FERROUS METALS AND NON-FERROUS ALLOYS
    • C22F1/00—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22F—CHANGING THE PHYSICAL STRUCTURE OF NON-FERROUS METALS AND NON-FERROUS ALLOYS
    • C22F1/00—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working
    • C22F1/04—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working of aluminium or alloys based thereon
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22F—CHANGING THE PHYSICAL STRUCTURE OF NON-FERROUS METALS AND NON-FERROUS ALLOYS
    • C22F1/00—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working
    • C22F1/04—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working of aluminium or alloys based thereon
    • C22F1/057—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working of aluminium or alloys based thereon of alloys with copper as the next major constituent
    • F—MECHANICAL ENGINEERING; LIGHTING; HEATING; WEAPONS; BLASTING
    • F28—HEAT EXCHANGE IN GENERAL
    • F28F—DETAILS OF HEAT-EXCHANGE AND HEAT-TRANSFER APPARATUS, OF GENERAL APPLICATION
    • F28F1/00—Tubular elements; Assemblies of tubular elements
    • F28F1/02—Tubular elements of cross-section which is non-circular
    • F28F1/022—Tubular elements of cross-section which is non-circular with multiple channels
    • F—MECHANICAL ENGINEERING; LIGHTING; HEATING; WEAPONS; BLASTING
    • F28—HEAT EXCHANGE IN GENERAL
    • F28F—DETAILS OF HEAT-EXCHANGE AND HEAT-TRANSFER APPARATUS, OF GENERAL APPLICATION
    • F28F2215/00—Fins
    • F—MECHANICAL ENGINEERING; LIGHTING; HEATING; WEAPONS; BLASTING
    • F28—HEAT EXCHANGE IN GENERAL
    • F28F—DETAILS OF HEAT-EXCHANGE AND HEAT-TRANSFER APPARATUS, OF GENERAL APPLICATION
    • F28F2275/00—Fastening; Joining
    • F28F2275/04—Fastening; Joining by brazing
    • Y—GENERAL TAGGING OF NEW TECHNOLOGICAL DEVELOPMENTS; GENERAL TAGGING OF CROSS-SECTIONAL TECHNOLOGIES SPANNING OVER SEVERAL SECTIONS OF THE IPC; TECHNICAL SUBJECTS COVERED BY FORMER USPC CROSS-REFERENCE ART COLLECTIONS [XRACs] AND DIGESTS
    • Y10—TECHNICAL SUBJECTS COVERED BY FORMER USPC
    • Y10T—TECHNICAL SUBJECTS COVERED BY FORMER US CLASSIFICATION
    • Y10T428/00—Stock material or miscellaneous articles
    • Y10T428/12—All metal or with adjacent metals
    • Y10T428/12493—Composite; i.e., plural, adjacent, spatially distinct metal components [e.g., layers, joint, etc.]
    • Y10T428/12736—Al-base component
    • Y10T428/12764—Next to Al-base component

Definitions

  • the present invention relates to an aluminum alloy material, and more particularly to an aluminum alloy material that can be joined to another member by its own action without using a joining member such as a brazing filler metal or a filler metal.
  • the present invention also relates to a structure using the aluminum alloy material that is efficiently bonded and has almost no dimensional change or shape change before and after bonding, and a method for manufacturing the structure.
  • brazing methods In manufacturing a structure such as a heat exchanger having an aluminum alloy material as a constituent member, it is necessary to join aluminum alloy materials together or an aluminum alloy material and a different material.
  • Various methods are known for joining aluminum alloy materials, and brazing methods (brazing methods) are often used among them.
  • the brazing method is often used because it takes into account advantages such as being able to obtain a strong bond in a short time without melting the base material.
  • Examples of a method for producing a heat exchanger using a joining method of an aluminum alloy material by a brazing method include a method using a brazing sheet clad with a brazing material made of an Al—Si alloy; an extruded material coated with a powder brazing material And a method in which a brazing material is separately applied to a portion that needs to be joined after assembling each material (Patent Documents 1 to 3). Furthermore, the section of “3.2 Brazing sheet” in Non-Patent Document 1 describes details of these clad brazing sheets and powder brazing materials.
  • brazing methods have been developed in the manufacture of aluminum alloy structural bodies.
  • a method of using a brazing sheet in which a tube material is clad with a brazing material, or a method of separately applying Si powder or Si-containing wax to the tube material was adopted.
  • the tube material is used as a single layer, a method of using a brazing sheet in which a fin material is clad with a brazing material has been adopted.
  • Patent Document 4 describes a method of using a single-layer brazing sheet instead of the clad brazing sheet described above. In this method, it has been proposed to use a single layer brazing sheet for a heat exchanger for the tube material and the tank material of the heat exchanger.
  • brazing sheet In order to produce a clad material such as a brazing sheet, it is necessary to produce each layer separately and further to laminate them.
  • the use of a brazing sheet is against the demand for cost reduction of heat exchangers and the like. Also, the application of the powder brazing material is reflected in the product cost by the amount of the brazing material cost.
  • an aluminum alloy structure such as a heat exchanger
  • it can be said that it is preferable to perform bonding with a single layer material without using a brazing material.
  • a single-layer brazing sheet is easily applied, it is difficult to avoid the problem of deformation of members.
  • the present invention has been made based on the background as described above, and in manufacturing various aluminum alloy structures, while eliminating the increase in cost due to the use of multiple-layer members, An object is to provide a technique that does not cause a problem of deformation.
  • This joining method uses the following aluminum alloy material to join and assemble under specific conditions, and can be joined without a joining member such as a brazing material, and further, deformation before and after joining is extremely small. Has characteristics.
  • the present invention is an aluminum alloy material containing Si: 1.0% by mass to 5.0% by mass, Fe: 0.01% by mass to 2.0% by mass, the balance being Al and inevitable impurities.
  • Si intermetallic compounds with a circle equivalent diameter of 0.5 ⁇ 5 [mu] m is present 250 / mm 2 or more 7 ⁇ 10 5 cells / mm 2 or less in the aluminum alloy material cross section,
  • the present invention is basically characterized in that a liquid phase generated when an aluminum alloy material having the above composition is heated is used for bonding. First, the liquid phase generation mechanism will be described.
  • FIG. 1 schematically shows a phase diagram of an Al—Si alloy which is a typical binary eutectic alloy.
  • an aluminum alloy material having a Si concentration of c1 is heated, generation of a liquid phase starts at a temperature T1 near the eutectic temperature (solidus temperature) Te.
  • T1 near the eutectic temperature (solidus temperature) Te.
  • Te eutectic temperature
  • FIG. 2A crystal precipitates are distributed in the matrix divided by the grain boundaries.
  • FIG. 2B shows the crystal grain boundary with a large segregation of the crystal precipitate distribution melts to become a liquid phase.
  • the periphery of the Si crystal precipitate particles and intermetallic compounds which are the main additive element components dispersed in the matrix of the aluminum alloy material, melts into a spherical shape to form a liquid phase.
  • this spherical liquid phase generated in the matrix is re-dissolved in the matrix with the passage of time and temperature due to the interfacial energy, and the grain boundary and the surface are diffused by the solid phase diffusion. Move to.
  • FIG. 1 when the temperature rises to T2, the liquid phase amount increases from the state diagram.
  • this spherical liquid phase generated in the matrix is re-dissolved in the matrix with the passage of time and temperature due to the interfacial energy, as in the case of c1, and diffused in the solid phase. To move to the grain boundary or surface. When the temperature rises to T3, the liquid phase amount increases from the state diagram.
  • the joining method using the aluminum alloy material according to the present invention utilizes a liquid phase generated by local melting inside the aluminum alloy material as described above. And it can implement
  • the aluminum alloy material of the present invention is molded to produce a structure such as a tube, fin, or plate, and heat treatment is performed at a temperature of about 600 ° C.
  • the liquid phase is generated from a part of the aluminum alloy material. It is generated and oozes out on the surface of the material and can be joined, and a heat exchanger can be manufactured without using a joining member such as a brazing material.
  • the material strength is mainly composed of an unmelted matrix (a portion of the aluminum material excluding the intermetallic compound) and an intermetallic compound that does not contribute to liquid phase generation. Therefore, although the aluminum alloy material according to the present invention is in a state where a part of the melt is generated during joining, the aluminum alloy material can have sufficient strength to maintain the shape. Therefore, the structure manufactured according to the present invention has a feature that there is almost no dimensional change or shape change due to strength reduction during bonding. Due to such characteristics, the aluminum alloy material of the present invention can be suitably used as a thin material such as a fin that is easily deformed during bonding.
  • the present invention utilizes the liquid phase of the aluminum alloy material, and the specific feature of the present invention is that, as the first aspect, the Si concentration as the aluminum alloy material is 1.0 mass% to 5 mass%. 0.0% by mass, Fe: 0.01% by mass to 2.0% by mass of Al—Si—Fe based alloy as a basic composition, and Si based intermetallic compound and Al based intermetallic compound in the metal structure Exists in a predetermined area density range in the cross section. Therefore, these features will be described below. In the following, “mass%” is simply referred to as “%”.
  • Si is an element that generates an Al-Si liquid phase and contributes to bonding.
  • Si concentration is defined as 1.0% to 5.0%.
  • the Si concentration is preferably 1.5% to 3.5%, more preferably 2.0% to 3.0%.
  • the amount of the liquid phase that oozes out increases as the plate thickness increases and the heating temperature increases, so the amount of liquid phase required during heating depends on the amount of Si and bonding required depending on the structure of the structure to be manufactured. It is desirable to adjust the heating temperature.
  • Fe in addition to the effect of improving the strength by slightly dissolving in the matrix, Fe has the effect of dispersing as a crystallized substance and preventing a decrease in strength particularly at high temperatures.
  • the addition amount of Fe is less than 0.01%, not only the above effect is small, but also high purity metal must be used and the cost increases.
  • it exceeds 2.0% a coarse intermetallic compound is produced at the time of casting, causing a problem in manufacturability.
  • the corrosion resistance decreases.
  • the addition amount of Fe is set to 0.01% to 2.0%.
  • a preferable addition amount of Fe is 0.2% to 1.0%.
  • the aluminum alloy material according to the present invention is characterized in that Si-based intermetallic compounds having a circle-equivalent diameter of 0.5 to 5 ⁇ m are present in a cross section of 250 pieces / mm 2 or more and 7 ⁇ 10 5 pieces / mm 2 or less.
  • the Si-based intermetallic compound includes (1) simple substance Si and (2) a part of the simple substance Si containing elements such as Ca and P, and the liquid described in the liquid phase generation process described above. It is an intermetallic compound that contributes to phase formation.
  • the cross section is an arbitrary cross section of the aluminum alloy material, for example, a cross section along the thickness direction or a cross section parallel to the plate material surface. From the viewpoint of simplicity of material evaluation, it is preferable to adopt a cross section along the thickness direction.
  • dispersed particles of an intermetallic compound such as Si particles dispersed in an aluminum alloy material react with the surrounding matrix at the time of bonding to generate a liquid phase. Therefore, the finer the dispersed particles of the intermetallic compound, the larger the area where the particles and the matrix are in contact. Therefore, the finer the dispersed particles of the intermetallic compound, the more easily the liquid phase is generated at the time of bonding heating, and good bonding properties are obtained. This effect is more remarkable when the bonding temperature is close to the solidus or when the heating rate is high.
  • the equivalent circle diameter is defined as 0.5 to 5 ⁇ m
  • the existence ratio is 250 / mm 2 or more and 7 ⁇ 10 5 / mm 2 in cross section.
  • the existence ratio of the Si-based intermetallic compound is 250 / mm 2 or more and 7 ⁇ 10 5 / mm 2 or less.
  • the existence ratio is preferably 1 ⁇ 10 3 pieces / mm 2 or more and 1 ⁇ 10 5 pieces / mm 2 or less.
  • an Al-based intermetallic compound exists as dispersed particles.
  • This Al-based intermetallic compound is composed of Al-Fe-based, Al-Fe-Si-based, Al-Mn-Si-based, Al-Fe-Mn-based, Al-Fe-Mn-Si-based compounds, etc. It is an intermetallic compound to be formed.
  • These Al-based intermetallic compounds unlike Si-based intermetallic compounds, do not contribute significantly to the liquid phase generation, but are dispersed particles that bear the material strength together with the matrix.
  • the Al-based intermetallic compound having an equivalent circle diameter of 0.5 to 5 ⁇ m needs to be present in the material cross section in a range of 100 / mm 2 to 7 ⁇ 10 5 / mm 2 . In the case of less than 100 pieces / mm 2 , deformation due to strength reduction occurs. On the other hand, when it exceeds 7 ⁇ 10 5 pieces / mm 2 , the recrystallization nuclei increase, the crystal grains become finer, and deformation occurs. As described above, the Al-based intermetallic compound is present at a rate of 100 / mm 2 or more and 7 ⁇ 10 5 / mm 2 or less.
  • the existence ratio is preferably 1 ⁇ 10 3 pieces / mm 2 or more and 1 ⁇ 10 5 pieces / mm 2 or less.
  • the equivalent circle diameter of the dispersed particles can be determined by performing SEM observation (reflection electron image observation) of the cross section.
  • the equivalent circle diameter means the equivalent circle diameter. It is preferable to obtain the equivalent circle diameter of the dispersed particles before joining by image analysis of the SEM photograph.
  • the Si-based intermetallic compound and the Al-based intermetallic compound can also be distinguished by contrast contrast by SEM-reflection electron image observation.
  • the metal species of the dispersed particles can be more accurately specified by EPMA (X-ray microanalyzer) or the like.
  • the aluminum alloy material according to the present invention having characteristics in the Si and Fe concentration ranges and the metal structure can be joined by its own joining property and can be used as a constituent member of various aluminum alloy structures.
  • the aluminum alloy material according to the present invention is defined by adding Si and Fe as essential elements in order to fulfill the basic function of bondability.
  • the aluminum alloy material according to the present invention has a predetermined amount of Mn in addition to the addition amounts of Si and Fe defined in the first embodiment in the second embodiment.
  • Mg and Cu are further added as essential elements.
  • the surface density in the cross section of the Si-based intermetallic compound and the Al-based intermetallic compound is defined in the same manner as in the first embodiment.
  • Mn is an important additive element that forms an Al—Mn—Si-based intermetallic compound with Si and acts as dispersion strengthening, or is a solid additive that improves the strength by solid solution strengthening by solid solution in the aluminum matrix. . If the amount of Mn added exceeds 2.0%, a coarse intermetallic compound is easily formed and the corrosion resistance is lowered. Therefore, the amount of Mn added is 2.0% or less. A preferable Mn addition amount is 0.05% to 2.0%. In the present invention, not only Mn but also other alloy components include 0% when the amount is less than a predetermined amount.
  • Mg undergoes age hardening by Mg 2 Si after bonding heating, and the strength is improved by this age hardening.
  • Mg is an additive element that exhibits the effect of improving the strength. If the amount of Mg added exceeds 2.0%, it reacts with the flux to form a high melting point compound, so that the bondability is significantly lowered. Therefore, the amount of Mg added is set to 2.0% or less. A preferable amount of Mg is 0.05% to 2.0%.
  • Cu is an additive element that improves the strength by solid solution in the matrix.
  • the amount of Cu added exceeds 1.5%, the corrosion resistance decreases. Therefore, the amount of Cu added is 1.5% or less.
  • a preferable addition amount of Cu is 0.05% to 1.5%.
  • Ti, V, Cr, Ni and Zr can be selectively added alone or in combination as elements other than the essential elements. Each selective additive element is described below.
  • Ti and V have the effect of preventing the progress of corrosion in the plate thickness direction by being dissolved in a layer, in addition to improving the strength by solid solution in the matrix. If it exceeds 0.3%, giant crystallized matter is generated, which impairs moldability and corrosion resistance. Therefore, the addition amount of Ti and V is preferably 0.3% or less, and more preferably 0.05% to 0.3%.
  • the amount of Cr added is preferably 0.3% or less, and more preferably 0.05% to 0.3%.
  • the amount of Ni added is preferably in the range of 2.0% or less, and more preferably in the range of 0.05% to 2.0%. When the Ni content exceeds 2.0%, it becomes easy to form a coarse intermetallic compound, and the workability is lowered and the self-corrosion resistance is also lowered.
  • the amount of Zr added is preferably 0.3% or less, and more preferably 0.05% to 0.3%.
  • selective additive elements for improving corrosion resistance may be added.
  • selective additive elements for improving corrosion resistance include Zn, In, and Sn.
  • Addition of Zn is effective in improving corrosion resistance due to sacrificial anticorrosive action.
  • Zn is dissolved almost uniformly in the matrix, but when a liquid phase is generated, it dissolves into the liquid phase and concentrates in the liquid phase. When the liquid phase oozes out to the surface, the Zn concentration in the oozed portion increases, so that the corrosion resistance is improved by the sacrificial anodic action.
  • the sacrificial anticorrosion action for preventing corrosion of tubes and the like can be exerted by using the aluminum alloy material of the present invention for fins. If the amount of Zn added exceeds 6.0%, the corrosion rate increases and the self-corrosion resistance decreases. Therefore, the amount of Zn added is preferably 6.0% or less, more preferably 0.05% to 6.0%.
  • the addition amount of Sn and In is preferably 0.3% or less, and more preferably 0.05% to 0.3%.
  • a selective element for further improving the bondability may be further added by improving the liquid phase characteristics.
  • these 1 type (s) or 2 or more types are added as needed. More preferable ranges of these elements are Be: 0.0001% to 0.1%, Sr: 0.0001% to 0.1%, Bi: 0.0001% to 0.1%, Na: 0 0.0001% to 0.1% or less, Ca: 0.0001% to 0.05% or less.
  • These trace elements can improve the bondability by fine dispersion of Si particles, improvement in fluidity of the liquid phase, and the like.
  • both Fe and Mn together with Si form an Al—Fe—Mn—Si based intermetallic compound. Since Si that forms an Al—Fe—Mn—Si-based intermetallic compound has a small contribution to the formation of the liquid phase, the bondability is lowered. Therefore, when adding Fe and Mn in the aluminum alloy material according to the present invention, it is preferable to pay attention to the amount of Si, Fe, and Mn added. Specifically, when the contents (mass%) of Si, Fe, and Mn are S, F, and M, respectively, the relational expression of 1.2 ⁇ S ⁇ 0.3 (F + M) ⁇ 3.5 is satisfied. Is preferred. When S-0.3 (F + M) is less than 1.2, bonding is insufficient. On the other hand, when S-0.3 (F + M) is larger than 3.5, the shape is likely to change before and after joining.
  • the aluminum alloy material that generates the liquid phase of the present invention preferably has a difference between the solidus temperature and the liquidus temperature of 10 ° C. or more.
  • this difference is preferably set to 10 ° C. or more.
  • binary alloys having a composition satisfying this condition include Al—Si alloys, Al—Si—Mg alloys, Al—Si—Cu alloys, Al—Si—Zn alloys, and Al—Si—Cu—. Mg type etc. are mentioned.
  • it becomes easy to control to an appropriate liquid phase amount so that the difference of solidus temperature and liquidus temperature becomes large. Therefore, the upper limit of the difference between the solidus temperature and the liquidus temperature is not particularly limited.
  • a layer mainly composed of Zn can be formed on the surface of the aluminum alloy material.
  • Zn present in the layer formed on the surface of the aluminum alloy material forms a concentration distribution in which the Zn concentration decreases from the surface toward the inside by solid solution and diffusion into the alloy during bonding heating.
  • Such a Zn concentration distribution corresponds to the pride of the pitting corrosion potential, and the progress of corrosion inside the aluminum alloy material can be significantly suppressed by the sacrificial anticorrosive action.
  • Examples of a method for providing a layer mainly composed of Zn on the surface of an aluminum alloy material include Zn spraying using pure Zn or an Al—Zn alloy; Zn substitution flux coating; Zn powder coating; Zn plating; In any of the methods, if the amount of Zn applied is too small, the sacrificial anticorrosive action becomes insufficient. If the amount of Zn applied is too large, the corrosion rate increases and the self-corrosion resistance decreases. Therefore, Zn amount applied is preferably 1 ⁇ 30g / m 2, more preferably 5 ⁇ 20g / m 2.
  • the aluminum alloy material of the present invention can be manufactured using a continuous casting method, a DC (Direct Hill) casting method, or an extrusion method.
  • the continuous casting method is not particularly limited as long as it is a continuous casting method such as a twin roll type continuous casting and rolling method or a twin belt type continuous casting method.
  • the twin-roll type continuous casting and rolling method is a method in which molten aluminum is supplied between a pair of water-cooled rolls from a refractory hot-water supply nozzle, and a thin plate is continuously cast and rolled.
  • the Hunter method, the 3C method, and the like are known. ing.
  • twin belt type continuous casting method is a method in which molten metal is poured between rotating belts facing each other up and down and solidified by cooling from the belt surface to form a slab.
  • This is a continuous casting method in which a slab is continuously drawn out and wound into a coil.
  • the cooling rate during casting is several to several hundred times faster than the DC casting method.
  • the cooling rate in the DC casting method is 0.5 to 20 ° C./sec
  • the cooling rate in the twin-roll continuous casting and rolling method is 100 to 1000 ° C./sec.
  • the dispersed particles generated during casting have a feature of being finely and densely distributed as compared with the DC casting method.
  • the dispersed particles distributed at a high density react with a matrix around the dispersed particles at the time of bonding, and can easily generate a large amount of liquid phase, thereby obtaining good bonding properties.
  • the speed of the rolled plate at the time of casting by the twin roll type continuous casting and rolling method is preferably 0.5 m / min or more and 3 m / min or less.
  • the casting speed affects the cooling rate. When the casting speed is less than 0.5 m / min, a sufficient cooling rate cannot be obtained and the compound becomes coarse. On the other hand, when it exceeds 3 m / min, the aluminum material is not sufficiently solidified between rolls during casting, and a normal plate-shaped ingot cannot be obtained.
  • the molten metal temperature when casting by the twin roll type continuous casting and rolling method is preferably in the range of 650 to 800 ° C.
  • the molten metal temperature is the temperature of the head box immediately before the hot water supply nozzle.
  • 650 ° C. huge intermetallic compound dispersed particles are generated in the hot water supply nozzle, and these are mixed into the ingot to cause a sheet break during cold rolling.
  • the molten metal temperature exceeds 800 ° C., the aluminum material is not sufficiently solidified between the rolls during casting, and a normal plate-shaped ingot cannot be obtained.
  • a more preferable molten metal temperature is 680 to 750 ° C.
  • the thickness of the cast plate is preferably 2 mm to 10 mm. In this thickness range, the solidification rate at the central portion of the plate thickness is fast, and a uniform structure can be easily obtained.
  • the cast plate thickness is less than 2 mm, the amount of aluminum passing through the casting machine per unit time is small, and it becomes difficult to stably supply the molten metal in the plate width direction.
  • the cast plate thickness exceeds 10 mm, winding with a roll becomes difficult.
  • a more preferable cast plate thickness is 4 mm to 8 mm.
  • annealing may be performed once or more.
  • Appropriate tempering is selected according to the application. Usually, it is H1n or H2n tempered to prevent erosion, but an annealed material may be used depending on the shape and usage.
  • the casting speed of the slab or billet during casting it is preferable to control the casting speed of the slab or billet during casting. Since the casting speed affects the cooling rate, it is preferably 20 mm / min or more and 100 m / min or less. When the casting speed is less than 20 mm / min, a sufficient cooling rate cannot be obtained and the compound becomes coarse. On the other hand, when it exceeds 100 m / min, the aluminum material is not sufficiently solidified during casting, and a normal ingot cannot be obtained. A more preferable casting speed is 30 mm / min or more and 80 mm / min or less.
  • the slab thickness during DC continuous casting is preferably 600 mm or less. When the slab thickness exceeds 600 mm, a sufficient cooling rate cannot be obtained and the intermetallic compound becomes coarse. A more preferable slab thickness is 500 mm or less.
  • tempering is performed according to the application. This tempering is usually H1n or H2n to prevent erosion, but a soft material may be used depending on the shape and usage.
  • the aluminum alloy material according to the present invention is manufactured by an extrusion method
  • a homogenization process and hot extrusion may be performed as necessary after manufacturing a billet by DC casting.
  • tempering is performed according to the application.
  • a hot top casting method or a GDC casting method is used for the billet casting.
  • the aluminum alloy material of the present invention is provided in the form of a wrought material, a forged material, a casting, etc., but the shape of the wrought material is optimal from the viewpoint of joining properties and shape maintenance. Since the wrought material has a higher processing rate before its manufacture than forgings and castings, a state in which the intermetallic compound is finely divided is likely to appear. Therefore, the density of the Si-based intermetallic compound and the Al-based intermetallic compound can be increased, and as described above, there is an advantage that it is easy to achieve good bondability and shape maintenance.
  • the aluminum alloy structure is a structure in which two or more members are joined, and at least one of the members constituting the structure is made of the aluminum alloy material according to the present invention.
  • the method for producing an aluminum alloy structure according to the present invention includes combining an aluminum alloy material having the above composition as at least one member to be joined with another member to be joined, followed by heat treatment. A member to be joined is joined. In this heat treatment, inside the at least one member to be joined of the two or more members, the temperature is not less than the solidus temperature at which the liquid phase is generated and not more than the liquidus temperature, and the shape can be maintained by reducing the strength. Heating is performed for a time required for joining at a temperature equal to or lower than the disappearance temperature.
  • the heating conditions are particularly important among the bonding conditions in the above bonding method.
  • the heating condition the ratio of the mass of the liquid phase generated in the aluminum alloy material to the total mass of the aluminum alloy material which is at least one of the two or more members (hereinafter referred to as “liquid phase ratio”). It is necessary to join at a temperature that exceeds 0% and not more than 35%. Since the bonding cannot be performed unless the liquid phase is generated, the liquid phase ratio needs to be more than 0%. However, since joining becomes difficult when the liquid phase is small, the liquid phase ratio is preferably 5% or more. When the liquid phase ratio exceeds 35%, the amount of the liquid phase to be generated is too large, and the aluminum alloy material is greatly deformed during the heating to join, so that the shape cannot be maintained. As described above, the preferred liquid phase ratio is 5 to 30%. A more preferable liquid phase ratio is 10 to 20%.
  • the filling time it is preferable to consider the filling time, and it is preferable to set the time during which the liquid phase ratio is 5% or more to 30 seconds or more and 3600 seconds or less. More preferably, the time during which the liquid phase ratio is 5% or more is 60 seconds or more and 1800 seconds or less, whereby sufficient filling is performed and reliable bonding is performed. If the time during which the liquid phase ratio is 5% or more is less than 30 seconds, the joint may not be sufficiently filled with the liquid phase. On the other hand, if it exceeds 3600 seconds, the deformation of the aluminum material may proceed. In the bonding method according to the present invention, the liquid phase moves only in the very vicinity of the bonded portion, so that the time required for filling does not depend on the size of the bonded portion.
  • the joining temperature may be 580 ° C. to 620 ° C.
  • the holding time at the joining temperature may be about 0 to 10 minutes.
  • 0 minutes means that the cooling is started as soon as the temperature of the member reaches a predetermined joining temperature.
  • you may adjust a heating condition according to a composition More preferably, it is 30 seconds to 5 minutes.
  • the liquid phase ratio defined in the present invention can be usually obtained by lever principle from the alloy composition and the maximum attainable temperature using an equilibrium diagram.
  • the phase diagram can be used to determine the liquid phase ratio using the principle of leverage.
  • the liquid phase ratio can be obtained using equilibrium calculation diagram software.
  • the equilibrium calculation phase diagram software incorporates a technique for determining the liquid phase ratio based on the lever principle using the alloy composition and temperature.
  • Equilibrium calculation state diagram software includes Thermo-Calc; Thermo-Calc Software AB, etc.
  • the heating atmosphere in the heat treatment is preferably a non-oxidizing atmosphere substituted with nitrogen, argon or the like.
  • better bondability can be obtained by using a non-corrosive flux.
  • non-corrosive flux coating method examples include a method of sprinkling the flux powder after assembling the members to be joined, a method of spraying the flux powder suspended in water, and the like.
  • the adhesion of the coating can be improved by mixing and applying a binder such as an acrylic resin to the flux powder.
  • non-corrosive flux used for obtaining the normal flux function examples include KAlF 4 , K 2 AlF 5 , K 2 AlF 5 .H 2 O, K 3 AlF 6 , AlF 3 , KZnF 3 , K 2 SiF 6 and the like.
  • Fluoride flux, cesium flux such as Cs 3 AlF 6 , CsAlF 4 .2H 2 O, Cs 2 AlF 5 .H 2 O, chloride flux, and the like.
  • Necessary bonding characteristics can be obtained by the heat treatment and the control of the heating atmosphere described above.
  • the shape of the structure may not be maintained if the stress generated in the structure is too high.
  • the liquid phase ratio at the time of joining increases, the shape can be maintained better when the stress generated in the structure is kept at a relatively small stress.
  • the maximum value of the stresses generated in the joined member generated by the liquid phase among two or more members is P (kPa), and the liquid phase When the rate is V (%), a very stable junction can be obtained if the condition of P ⁇ 460-12V is satisfied.
  • the value indicated by the right side (460-12V) of this equation is the critical stress, and if a stress exceeding this is applied to the aluminum alloy material that generates a liquid phase, there is a possibility that large deformation will occur.
  • P ⁇ 460 using each stress P and liquid phase ratio V for each of the plurality of members to be joined It is preferable to perform the bonding so that ⁇ 12V is calculated and all the plurality of members to be bonded satisfy the above formula simultaneously.
  • the stress generated at each part in each member to be joined is obtained from the shape and load. For example, it can be calculated using a structural calculation program or the like.
  • the surface form of the joint as well as the pressure of the joint may affect the bondability, and a smoother surface can be obtained when both surfaces are smooth.
  • the sum of the arithmetic average undulations Wa1 and Wa2 obtained from the unevenness of the surfaces of both of the joined members before joining is Wa1 + Wa2 ⁇ 10 ( ⁇ m).
  • the arithmetic mean waviness Wa1 and Wa2 are defined by JISB0633, and the cut-off value is set so that the wavelength becomes uneven between 25 and 2500 ⁇ m, and the waviness curve measured with a laser microscope or a confocal microscope. It is requested from.
  • the structure may be formed by spraying Zn or applying Zn-substituted flux on the surface of the aluminum alloy material according to the present invention. Further, the structure after the heat treatment may be subjected to surface treatment such as chromate treatment or non-chromate treatment to improve corrosion resistance.
  • the aluminum alloy structure manufactured by the method for manufacturing an aluminum alloy structure described above has an advantage that the size and shape of the structure hardly change before and after joining. This is because the liquid phase is generated from the inside of the aluminum alloy material, which is the member to be joined, according to the mechanism described above, but the amount of the liquid phase to be generated is controlled within an appropriate range, and slip deformation along the crystal grain boundary etc. during joining This is because it is difficult to occur.
  • the effect of maintaining the shape of the bonded member during heating by the matrix or the intermetallic compound that does not contribute to the generation of the liquid phase is also a factor of the above-described advantage.
  • the aluminum alloy structure according to the present invention has suitable metallographic characteristics in the vicinity of the joint portion of at least one member of the joined members. That is, the aluminum alloy material joined by the method according to the present invention has a structure in which many intermetallic compounds and the like exist in the crystal grain boundaries. As is clear from the liquid phase generation mechanism shown in FIG. 2, the crystal grain boundary becomes one of the liquid phase outflow paths in the process of generating the liquid phase and flowing out. There is a liquid phase. Accordingly, when cooled thereafter, the liquid phase is solidified, so that an Si-based intermetallic compound and an Al-based intermetallic compound are generated at the crystal grain boundaries.
  • the number of triple points at the grain boundaries in which is present is a ratio of 50% or more of the number of triple points at all grain boundaries.
  • the triple point of the crystal grain boundary means a point (triple point) where at least three crystal grain boundaries of the matrix intersect when the cross section of the material is observed.
  • intermetallic compound The Si-based intermetallic compound and the Al-based intermetallic compound existing in the triple point of the grain boundary (hereinafter, a combination of both is referred to as “intermetallic compound”) is a second phase dispersion having a dispersion strengthening action. It works as particles and exerts the function of strengthening the members constituting the structure. Further, this intermetallic compound has an effect of suppressing the growth of crystal grains during cooling after heating for joining members. Furthermore, when the joined structure is reheated, the effect of suppressing the coarsening of crystal grains of the members constituting the structure is exhibited. These effects are not sufficient when the above-mentioned ratio of the triple points of the crystal grain boundary where the intermetallic compound exists is less than 50%.
  • the number of triple points at the crystal grain boundary where an intermetallic compound having an equivalent circle diameter of 1 ⁇ m or more exists among the triple points at all crystal grain boundaries is 50% or more. Further, this ratio is preferably 80% or more. Note that the upper limit of this ratio is 100%.
  • the intermetallic compound present at the triple point of the crystal grain boundary includes an Al-based intermetallic compound and a Si-based intermetallic compound.
  • the Si-based intermetallic compound is an intermetallic compound in which Fe, Mn, or the like is dissolved in Si.
  • Al-based intermetallic compounds include Al-Fe-based, Al-Fe-Si-based, Al-Mn-Si-based, Al-Fe-Mn-based, Al-Fe-Mn-Si-based compounds, etc. It is the produced intermetallic compound.
  • the cross section of the member constituting the structure of the present invention is mechanically polished and etched with a Keller solution or the like to identify the position of the intermetallic compound.
  • the crystal grain boundary in the same cross section is clarified by an anodic oxidation method, and the position of the triple point of the crystal grain boundary is identified. By comparing the two, the ratio of the triple point of the crystal grain boundary where the intermetallic compound having an equivalent circle diameter of 1 ⁇ m or more exists among the triple points of all the crystal grain boundaries is determined.
  • intermetallic compounds are formed discontinuously at the grain boundaries, or Al phases and intermetallic compound phases are alternately arranged.
  • a eutectic structure may be formed.
  • the crystal grain boundary since the crystal grain boundary becomes unclear, the crystal grain boundary may be observed as an intermittent line, and the position of the triple point of the crystal grain boundary becomes unclear.
  • the intermetallic compound or the eutectic structure is regarded as a part of the crystal grain boundary, and a continuous virtual line is drawn so as to follow the crystal grain boundary to determine the triple point of the crystal grain boundary. As shown in FIG.
  • the entire area of the part is set as the crystal grain boundary as shown in FIG. .
  • a region where three crystal grain boundaries virtually intersect is regarded as a triple point of the crystal grain boundary.
  • the triple point in this case is an area portion obtained by combining the crystal grain boundary portions in the region where the crystal grain boundaries intersect.
  • the intermetallic compound should just be formed even in part in this area part.
  • EPMA X-ray microanalyzer
  • EPMA is used to perform surface components of elements such as Si and Fe in the cross section of the members constituting the structure. Since the Si concentration is low near the crystal grain boundary, the crystal grain boundary can be identified.
  • the intermetallic compound can be identified in a portion where the element concentration of Si, Fe or the like is high. The position of the crystal grain boundary and the intermetallic compound can also be identified using SEM observation (reflection electron image observation) of the cross section.
  • the aluminum alloy structure formed according to the present invention has suitable metallographic features in the vicinity of the joint of at least one member of the joined members. That is, in the joint portion of the aluminum alloy material according to the present invention, in the liquid phase generation mechanism described above, the periphery of the Si particles remains in the matrix to some extent while being spherically melted, and the eutectic structure as shown in FIG. A large number of structures are dispersed in the crystal grains of the matrix (hereinafter simply referred to as “intra-grain”). According to the present inventors, in the aluminum alloy structure according to the present invention, when there is a good balance between good bondability and material strength at the time of bonding, the major axis of 3 ⁇ m or more present in the grains after bonding is obtained.
  • the eutectic structure possessed is preferably 10 pieces / mm 2 to 3000 pieces / mm 2 in terms of cross-sectional area density.
  • the preferable condition on the metal structure when the surface density of the intragranular eutectic structure is less than 10 pieces / mm 2 , it is difficult to maintain the strength during bonding heating due to too much liquid phase contributing to bonding. There is a case.
  • the surface density of the intragranular eutectic structure exceeds 3000 / mm 2 , the liquid phase contributing to the bonding is small and the bonding property may be lowered.
  • Such an eutectic structure within the grain has a shape close to a sphere because the liquid phase formed by melting around the Si particles during heating solidifies into a eutectic structure by solidifying during cooling.
  • the liquid phase formed by melting around the Si particles during heating solidifies into a eutectic structure by solidifying during cooling.
  • FIG. 2 it is observed as a circular eutectic structure in cross-sectional observation.
  • a eutectic structure having a shape along the Al-based intermetallic compounds may be formed. is there.
  • the cross section of the member constituting the structure of the present invention is mechanically polished and etched with a Keller solution or the like to identify the position of the eutectic structure. Since the eutectic structure has a structure in which Si-based intermetallic compound phases and Al phases are arranged minutely and alternately, this can be distinguished. Further, the position of the crystal grain boundary in this cross section is identified by the anodic oxidation method. By comparing the two, the number of eutectic structures having a major axis of 3 ⁇ m or more present in the crystal grains is measured and converted to the surface density.
  • EPMA X-ray microanalyzer
  • surface components of elements such as Si and Fe in a cross section of a member constituting the structure are performed.
  • the eutectic structure can be identified because the portions where the Si concentration is high and the portions where the Si concentration is low are arranged alternately and finely. Further, since the Si concentration is low near the crystal grain boundary, the crystal grain boundary can be identified.
  • the eutectic structure can also be identified by SEM observation (reflection electron image observation) of the cross section. In that case, the grain boundary is identified using the SEM / EBSB method.
  • the aluminum alloy structure having the metal structure as described above is manufactured by adjusting the dimensions and composition of the aluminum alloy material according to the present invention and adjusting the heating conditions in consideration of the composition. For example, in the case where the thickness of the aluminum alloy material that is the member to be joined is thick, or in the aluminum alloy member that is disposed in a portion where the temperature during joining tends to be high, it is sufficient to use a material having a low Si addition amount. A liquid phase amount can be secured. Specifically, in the case of a fin material having a plate thickness of 30 ⁇ m to 100 ⁇ m, it is preferable that the Si addition amount is about 1.5% to 3.5% and the heating temperature is about 580 ° C. to 620 ° C.
  • the eutectic structure in the grains is 20 to 500 pieces / mm 2 .
  • the Si addition amount of the aluminum alloy material to be bonded is 1.5% so that the cross-sectional surface density of the eutectic structure in the grains is 10 to 3000 / mm 2.
  • a bonded body having good bonding properties can be obtained.
  • by adding 0.3% or more of Mn there is an effect of reducing the intragranular eutectic structure.
  • the aluminum alloy structure according to the present invention is a structure composed of two or more members, and at least one member is composed of the aluminum alloy material according to the present invention.
  • various heat exchangers can be mentioned.
  • the heat exchanger is configured by appropriately combining various members such as a fin material, a tube material, a plate material, and a tank material depending on the application and use conditions.
  • the aluminum alloy material which concerns on this invention can comprise the various members of these heat exchangers.
  • a tube material and a tank material are produced from the aluminum alloy material according to the present invention, and further combined with a single-layer fin material (bare fin material) and subjected to a predetermined heat treatment.
  • a fin material and a plate material are produced with the aluminum alloy material according to the present invention, combined with a tube material (an extruded material or an electro-sewn bare tube material) in which a brazing material is not disposed, and a predetermined heat treatment is performed. It is possible to manufacture a heat exchanger.
  • a laminate-type heat exchanger can be manufactured by press-molding and laminating plate materials.
  • the aluminum alloy material according to the present invention can also be used for applications such as a heat sink and a laminated structure oil cooler.
  • a structure using a single layer material in which such a brazing material is not disposed may be less rigid at high temperatures than a structure using a conventional material. Therefore, when heat treatment is performed, a structure with higher dimensional accuracy can be obtained by setting the structure using a jig made of a material such as iron that can withstand high temperatures.
  • a heat exchanger can be easily manufactured by separately manufacturing a comb-blade shaped extruded material and an extruded material having a hollow portion and joining these two extruded materials. Moreover, it can also be set as products, such as an oil cooler and a heat sink corresponding to required size, by making two extrusion materials into a laminated structure.
  • the aluminum alloy material according to the present invention is joined by a joining method different from a conventional joining method such as a brazing method, and can be joined to various members to be joined in a single layer state. And there is almost no change in dimension or shape before and after joining.
  • the joining method using the aluminum alloy material according to the present invention can join the members to be joined without using a joining member such as a brazing material.
  • the aluminum alloy structure which concerns on this invention can respond to the request
  • FIG. 3 is a schematic diagram showing a phase diagram of an Al—Si alloy as a binary eutectic alloy. It is explanatory drawing which shows the production
  • FIG. 5 is a perspective view of a three-stage test piece (mini-core) used in the first to third embodiments. It is a perspective view which shows a part of shape of the extrusion tube used for the test piece of 3rd Embodiment. It is a schematic diagram which shows a crystal grain boundary and its triple point. It is explanatory drawing which shows the method of discriminating the triple point of a crystal grain boundary.
  • First Embodiment First, test materials for aluminum alloys B1 to B59 and B77 to B98 in Tables 3 to 5 were manufactured using aluminum alloys having the compositions shown in Tables 1 and 2. In the alloy composition shown in Table 1, “ ⁇ ” indicates that it is below the detection limit, and “remainder” includes inevitable impurities.
  • the test materials B1 to B48, B52 to B57, and B84 were cast by a twin roll type continuous casting and rolling method.
  • the melt temperature at the time of casting by the twin roll type continuous casting and rolling method was 650 to 800 ° C., and the thickness of the cast plate was 7 mm.
  • the casting speed was variously changed as shown in Tables 3-5.
  • the obtained plate-shaped ingot was cold-rolled to 0.70 mm, and after intermediate annealing at 420 ° C. ⁇ 2 Hr, further cold-rolled to 0.050 mm to obtain a test material.
  • the arithmetic average waviness Wa of the test material was about 0.5 ⁇ m.
  • B49 to B51, B58 to B59, B77 to B83, B85 to B98 test materials were cast in a size of 100 mm ⁇ 300 mm by the DC casting method.
  • the casting speed was variously changed as shown in Tables 4 and 5.
  • the obtained slab was heated after chamfering and hot-rolled to a thickness of 3 mm. Thereafter, the rolled plate was cold-rolled to 0.070 mm, and after intermediate annealing at 380 ° C. ⁇ 2 Hr, further cold-rolled to 0.050 mm to obtain a test material.
  • the arithmetic average waviness Wa of the test material was about 0.5 ⁇ m.
  • test materials were evaluated for manufacturability in the production process.
  • the evaluation method for manufacturability is as follows: when a plate or slab is manufactured, no problem occurs in the manufacturing process and a sound plate or slab is obtained. A case where a problem occurred in the manufacturing process, such as a case where rolling became difficult due to the generation of a huge intermetallic compound, was evaluated as x.
  • the surface density of the intermetallic compound in the produced plate material was measured by SEM observation (reflection electron image observation) of the cross section along the plate thickness direction.
  • Si-based intermetallic compounds and Al-based intermetallic compounds were distinguished by contrast density in SEM observation.
  • SEM observation was performed on each sample for five fields, and the density of dispersed particles having a circle-equivalent diameter of 0.5 ⁇ m to 5 ⁇ m in the sample was measured by image analysis of SEM photographs of each field.
  • each test material was formed into a fin material having a width of 16 mm, a peak height of 7 mm, and a pitch of 2.5 mm. Further, the material having the composition b1 (Table 2) was molded into an electro-sewn tube material having an arithmetic average waviness Wa of 0.3 ⁇ m and a plate thickness of 0.4 mm. Then, the fin material and the tube material were combined and incorporated into a stainless steel jig, and a three-stage test piece (minicore) shown in FIG. 4 was produced. Test pieces (minicores) made from the fin material and tube material of each test material (B1 to B59, B77 to B98) are shown in Tables 3 to 5 as C1 to C59 and C77 to C98.
  • the mini-core was immersed in a 10% suspension of non-corrosive fluoride flux and dried, and then heated at 580 to 600 ° C. for 3 minutes in a nitrogen atmosphere to join the fin material and the tube material.
  • a compressive load of about 4 N was generated between the stainless steel jig and the mini-core due to the difference in thermal expansion coefficient between the stainless steel jig and the aluminum material.
  • a stress of about 10 kPa is generated on the joint surface between the fin and the tube.
  • the ratio of the fin height change before and after joining to the fin height before joining is 5% or less, ⁇ 5% to 10% or less, ⁇ 10% to 15% or less, ⁇ , 15% or more It was determined.
  • the bonded mini-core was filled with resin and polished, the cross-sectional structure of the member was observed with an optical microscope, and the surface density of the intragranular eutectic structure having a major axis of 3 ⁇ m or more was measured.
  • the cross-section of the mini-core after bonding is polished and etched with a Keller solution to identify the position of the intermetallic compound, and further, the crystal grain boundary in this cross-section is clarified by an anodic oxidation method. The position of was identified. The position of these intermetallic compounds and the position of the triple point of the crystal grain boundary were compared, and the ratio of the triple point of the crystal grain boundary where the intermetallic compound exists was determined.
  • Tables 3 to 5 show the evaluation results of the above mini-core joining test. Tables 3 to 5 also show the equilibrium liquid phase ratio at the heating temperature in each sample. The equilibrium liquid phase ratio is a value calculated by equilibrium state diagram calculation software.
  • Comparative Example C54 (alloy composition A68) since the Fe component exceeded the specified amount, a coarse intermetallic compound was generated, and rolling to the final plate pressure was impossible, resulting in a problem in manufacturability.
  • Comparative Example C55 (alloy composition A69) since the Mg content exceeded the specified amount, the joining rate was as low as 30%, and the joining was incomplete.
  • Comparative Example C56 (alloy composition A70) had a problem in manufacturability.
  • Comparative Example C57 (Alloy Composition A71) produced a huge intermetallic compound during casting, and could not be rolled to the final plate pressure, resulting in a problem in manufacturability.
  • Comparative Example C58 alloy A72
  • Be, Sr, and Bi exceeded the specified amounts, so the surface oxide film became thicker and the bonding rate decreased.
  • Comparative Example C59 alloy A73
  • Na and Ca exceeded the specified amounts
  • the oxide film on the surface became thick and the bonding rate decreased.
  • Comparative Example C93 alloy A88
  • Comparative Example C94 alloy composition A80
  • the alloy composition was within the specified range, but the surface density of the Si-based intermetallic compound was reduced, and the ratio of triple points at the grain boundaries where the intermetallic compound was present was also low. As a result, the joining rate decreased.
  • Comparative Examples C95 to 98 alloy compositions A89 to 92
  • a huge intermetallic compound was produced during casting as described above, and rolling to the final plate pressure was impossible, resulting in a problem in manufacturability.
  • Second Embodiment In this embodiment, the influence of the heating temperature, which is a bonding condition, was examined. As shown in Table 6, the material manufactured in the first embodiment was extracted and formed into the same fin material as in the first embodiment. And the test piece (mini-core) of 3 steps
  • the mini-core joined as described above was measured and evaluated in the same manner as in the first embodiment. Moreover, the fin height of the mini-core after joining was measured, and the dimensional change rate after joining with respect to before joining was calculated
  • the structure of the cross section of the member is observed, and the surface density of the intermetallic compound, the surface density of the intragranular eutectic structure having a major axis of 3 ⁇ m or more, and the triple points of all crystal grain boundaries
  • the ratio of the triple point of the crystal grain boundary where an intermetallic compound having an equivalent circle diameter of 1 ⁇ m or more exists was determined.
  • the evaluation results are shown in Table 6.
  • Comparative Examples C74 and C76 since the liquid phase ratio was too high, the shape could not be maintained and the deformation rate increased. In Comparative Example C75, the liquid phase rate was too low. Moreover, the ratio of the triple point of the crystal grain boundary where an intermetallic compound exists was also low. As a result, the joining rate decreased.
  • Third Embodiment In this embodiment, the effect of a layer containing Zn as a main component for improving extrusion moldability and corrosion resistance was examined.
  • a material having the composition shown in Table 7 (No. E1 to E24, E25, and E26) was DC cast to obtain a billet having a diameter of 150 mm.
  • “ ⁇ ” indicates that it is below the detection limit, and “remainder” includes inevitable impurities.
  • FIG. 5 is a perspective view showing a part of the flat extruded tube.
  • the arithmetic average waviness Wa of the test material was about 1 ⁇ m.
  • the extrudability of each specimen in hot extrusion was evaluated.
  • extrudability when hot extrusion is performed, a case where a sound extrudate is obtained by 10 m or more is marked as ⁇ , a case where the obtained sound extrudate is more than 0 m and less than 10 m is marked as ⁇ , and at the time of casting A case where a sound extrudate was not obtained due to generation of a coarse intermetallic compound (including a case where the obtained sound extrudate was 0 m) was evaluated as x.
  • Sample Nos. D25 to D39 shown in Table 9 a layer mainly composed of Zn was formed on the surface of the extruded tube.
  • Sample Nos. D40 to D42 shown in Table 9 are reference examples in which a layer containing Zn as a main component is not formed.
  • any one of Zn spraying, Zn substitution flux coating Zn powder coating and Zn plating was adopted.
  • the material of F1 composition (JISA3003 + 1.5Zn) in Table 7 (arithmetic mean waviness Wa is 0.3 ⁇ m, plate thickness 0.07 mm) was processed into a fin material.
  • the fin material was corrugated to a height of 7 mm.
  • Sample No. A flat extruded tube of D1 to D42, D43, and D44 and the fin material were combined and incorporated into a stainless steel jig, and a three-stage test piece (minicore) shown in FIG. 4 was produced.
  • mini-core a compressive load of about 4 N was generated between the stainless steel jig and the mini-core due to the difference in thermal expansion coefficient between the stainless steel jig and the aluminum material.
  • a stress of about 10 kPa is generated on the joint surface between the fin and the tube.
  • the mini-core thus produced is dipped in a 10% suspension of non-corrosive fluoride-based flux, dried, and then heated in a nitrogen atmosphere at 580 to 600 ° C. for 3 minutes to form a fin material and a tube material. Joined.
  • Sample No. In D13, D14, and D22 bonding was performed in a vacuum without applying a flux.
  • Sample No. In D12 a fluoride-based flux containing cesium was used.
  • Sample No. In D26 Zn substitution flux was applied and heated.
  • Sample No. D1 to D24, D43, and D44 were evaluated by obtaining the joining ratio of the tube and the fin as in the first embodiment. The presence or absence of tube collapse was also confirmed. Further, a CASS test was performed for 1000 h for corrosion resistance evaluation, and the presence or absence of corrosion penetrating the tube was confirmed. The case where there was no corrosion was marked with ⁇ , and the case where corrosion occurred was marked with ⁇ .
  • the structure of the cross section of the member is observed, and the surface density of the intragranular eutectic structure having a major axis of 3 ⁇ m or more, and the equivalent circle diameter of 1 ⁇ m or more among the triple points of all grain boundaries.
  • the ratio of the triple point of the crystal grain boundary where the intermetallic compound having s was present.
  • the surface density of dispersed particles of Si-based intermetallic compound and Al-based intermetallic compound having an equivalent circle diameter of 0.5 ⁇ m to 5 ⁇ m in the sample was measured. The evaluation results are shown in Table 8.
  • Comparative Example D16 (alloy composition E16), since the Si component is less than the specified value, a crystal in which an intermetallic compound having a circle-equivalent diameter of 1 ⁇ m or more exists among triple points of all grain boundaries. The ratio of triple points at grain boundaries was low. Moreover, the joining rate also decreased.
  • Comparative Example D17 (alloy composition E17)
  • the Si component exceeded the specified value, and the liquid phase ratio was too high.
  • Comparative Example D18 (alloy composition E18) since the Si component was less than the specified value, the ratio of the triple point of the crystal grain boundary where the intermetallic compound having an equivalent circle diameter of 1 ⁇ m or more was low was low. Moreover, the joining rate also decreased.
  • Comparative Example D19 (alloy composition E19), since the Si component exceeded the specified value, the extruded tube was crushed during bonding.
  • Comparative Example D20 to Comparative Example D24 were inferior in terms of corrosion resistance due to the occurrence of through holes in the CASS test results. These are attributed to the alloy composition, and Fe and Cu components (alloy composition E20), Mn component (alloy composition E21), Zn component (alloy composition E22), Mg component (alloy composition E23), Cr, This is because the Ti and V components (alloy composition E24) exceed specified values.
  • the sacrificial anticorrosive action works because the Zn layer is formed on the surface, and the corrosion depth is 0. .It was shallow with less than 60 mm.
  • the structure can be efficiently manufactured. Moreover, in this invention, the change of the dimension or shape before and behind joining of a joining member hardly arises. As described above, the aluminum alloy material according to the present invention, the structure using the aluminum alloy material, and the method for producing the same have significant industrial effects.

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Abstract

Le problème décrit par la présente invention consiste à mettre à disposition un matériau en alliage d'aluminium qui est utile dans diverses structures en alliage d'aluminium et qui peut être assemblé même sous forme d'une seule couche et ne subit pas de changement de forme avant ou après l'assemblage. Selon l'invention, le problème peut être résolu par un matériau en alliage d'aluminium qui contient 1 à 5 % en masse de Si et 0,01 à 2,0 % en masse de Fe, le reste étant de l'Al et des impuretés inévitables et dans lequel des particules de composé intermétallique à base de Si présentant des diamètres de cercle équivalent de 0,5 à 5 µm sont présentes dans la section en une quantité de 250 à 7×105 particules/mm2, tandis que des particules de composé intermétallique à base d'Al présentant des diamètres de cercle équivalent de 0,5 à 5 µm sont présentes en une quantité de 100 à 7×105 particules/mm2. Cette structure en alliage d'aluminium peut être produite par assemblage sous vide ou dans une atmosphère non oxydante à une température telle que le rapport massique d'une phase liquide formée dans le matériau en alliage d'aluminium à cette température au matériau en alliage d'aluminium se situe dans la plage de 5 à 35 %.
PCT/JP2012/075404 2011-12-02 2012-10-01 Matériau en alliage d'aluminium et structure en alliage d'aluminium et leur procédé de production WO2013080650A1 (fr)

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ES12853959.0T ES2613590T3 (es) 2011-12-02 2012-10-01 Material de aleación de aluminio y estructura de aleación de aluminio y proceso de producción de los mismos
KR1020147018291A KR101581607B1 (ko) 2011-12-02 2012-10-01 알루미늄 합금재를 이용한 열교환기용 핀재와 이를 포함하는 알루미늄 합금 구조체
EP12853959.0A EP2787094B1 (fr) 2011-12-02 2012-10-01 Matériau en alliage d'aluminium et structure en alliage d'aluminium et leur procédé de production
CN201280045064.2A CN103930577B (zh) 2011-12-02 2012-10-01 铝合金材料和铝合金结构体及其制造方法
JP2013506400A JP5337326B1 (ja) 2011-12-02 2012-10-01 アルミニウム合金材、ならびに、アルミニウム合金構造体及びその製造方法
US14/361,740 US9574253B2 (en) 2011-12-02 2012-10-01 Aluminum alloy material, aluminum alloy structure, and manufacturing method for same
IN1031MUN2014 IN2014MN01031A (fr) 2011-12-02 2012-10-01
BR112014013132-5A BR112014013132B1 (pt) 2011-12-02 2012-10-01 Membro de barbatana em uma única camada para um trocador de calor, método de fabricação para uma estrutura de liga de alumínio e estrutura de liga de alumínio
US15/411,739 US9903008B2 (en) 2011-12-02 2017-01-20 Aluminum alloy material, aluminum alloy structure, and manufacturing method for same

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* Cited by examiner, † Cited by third party
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CN103796347A (zh) * 2014-03-03 2014-05-14 南通华特铝热传输材料有限公司 用于家用空调ptc发热器的复合铝条
WO2014184880A1 (fr) * 2013-05-14 2014-11-20 株式会社Uacj Matériau d'alliage d'aluminium, dont une couche unique permet une fixation thermique ; procédé de fabrication de celui-ci ; et corps fixé en aluminium utilisant ledit matériau d'alliage d'aluminium
WO2014196183A1 (fr) * 2013-06-02 2014-12-11 株式会社Uacj Échangeur thermique et matériau d'ailette pour ledit échangeur thermique
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WO2022176420A1 (fr) * 2021-02-16 2022-08-25 株式会社Uacj Tôle en alliage d'aluminium et son procédé de production, et échangeur de chaleur

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* Cited by examiner, † Cited by third party
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WO2015141192A1 (fr) * 2014-03-19 2015-09-24 株式会社Uacj Matériau en alliage d'aluminium revêtu présentant d'excellentes résistance à la corrosion et aptitude au brasage et procédé de fabrication s'y rapportant
KR101603424B1 (ko) * 2014-07-14 2016-03-15 명화공업주식회사 주단조용 알루미늄 합금 및 이를 이용한 자동차 샤시구조 부품의 제조방법
JP2016035368A (ja) * 2014-08-04 2016-03-17 株式会社Uacj アルミニウム合金熱交換器およびその製造方法
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US10786051B2 (en) * 2015-03-27 2020-09-29 Ykk Corporation Element for slide fastener
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MX2017013469A (es) * 2015-04-28 2018-03-01 Consolidated Eng Company Inc Sistema y metodo para tratamiento termico de piezas fundidas de aleacion de aluminio.
RU2610578C1 (ru) * 2015-09-29 2017-02-13 Общество с ограниченной ответственностью "Объединенная Компания РУСАЛ Инженерно-технологический центр" Высокопрочный сплав на основе алюминия
US11085277B2 (en) 2015-10-07 2021-08-10 Benteler Steel/Tube Gmbh Seamless steel pipe, method of producing a high strength seamless steel pipe, usage of a seamless steel pipe and perforation gun
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US10538834B2 (en) 2015-12-18 2020-01-21 Novelis Inc. High-strength 6XXX aluminum alloys and methods of making the same
EP3390678B1 (fr) 2015-12-18 2020-11-25 Novelis, Inc. Alliages d'aluminium 6xxx haute résistance et leurs procédés d'élaboration
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CN115354178A (zh) * 2022-10-19 2022-11-18 山东裕航特种合金装备有限公司 石油钻探用铝合金管体及其制备方法

Citations (10)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
JPH036355A (ja) * 1989-05-31 1991-01-11 Showa Alum Corp 無電解Ｚｎメッキ用アルミニウム材の製造方法
JP2001262264A (ja) * 2000-03-21 2001-09-26 Kobe Steel Ltd 靱性および曲げ性に優れたＡｌ−Ｍｇ−Ｓｉ系Ａｌ合金板
JP2004332106A (ja) * 2003-04-15 2004-11-25 Nippon Light Metal Co Ltd プレス成形性および連続抵抗スポット溶接性に優れたアルミニウム合金板およびその製造方法
JP2008303405A (ja) 2007-06-05 2008-12-18 Mitsubishi Alum Co Ltd 熱交換器ヘッダプレート用アルミニウム合金材料および熱交換器用ろう付け体
JP2008308760A (ja) 2006-12-21 2008-12-25 Mitsubishi Alum Co Ltd ろう付によって製造される高強度自動車熱交換器用部材に用いられる、成形性と耐エロージョン性に優れた自動車熱交換器用高強度アルミニウム合金材、及びその製造方法
JP2009068056A (ja) * 2007-09-12 2009-04-02 Sumitomo Light Metal Ind Ltd レーザ溶接性に優れたアルミニウム合金板材
JP2009161835A (ja) 2008-01-09 2009-07-23 Sumitomo Light Metal Ind Ltd アルミニウム製熱交換器及びその製造方法
JP2010168613A (ja) 2009-01-21 2010-08-05 Furukawa-Sky Aluminum Corp 熱交換器用単層ブレージングシートおよびそれを使用した熱交換器
JP2012040611A (ja) * 2010-07-20 2012-03-01 Furukawa-Sky Aluminum Corp アルミニウム合金材を用い、耐食性に優れた構造体とその接合方法
JP2012051028A (ja) * 2010-08-06 2012-03-15 Furukawa-Sky Aluminum Corp アルミニウム合金材を用いた構造体とその接合方法

Family Cites Families (9)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
US4473110A (en) * 1981-12-31 1984-09-25 Union Carbide Corporation Corrosion protected reversing heat exchanger
JP3403333B2 (ja) * 1998-05-15 2003-05-06 古河電気工業株式会社 自動車用アルミニウム板材とその製造方法
DE10163039C1 (de) * 2001-12-21 2003-07-24 Daimler Chrysler Ag Warm- und kaltumformbares Bauteil aus einer Aluminiumlegierung und Verfahren zu seiner Herstellung
DE502004009801D1 (de) * 2003-01-23 2009-09-10 Rheinfelden Aluminium Gmbh Druckgusslegierung aus Aluminiumlegierung
CN100413986C (zh) * 2003-04-15 2008-08-27 日本轻金属株式会社 具有优异模压成型性及连续电阻点焊性的铝合金板及其生产方法
JP4669711B2 (ja) * 2005-02-17 2011-04-13 株式会社デンソー ブレージング用アルミニウム合金フィン材
JP3869846B2 (ja) * 2005-03-25 2007-01-17 神鋼アルコア輸送機材株式会社 アルミニウム合金板および熱交換器
US8247084B2 (en) 2010-05-18 2012-08-21 Kobe Steel, Ltd. Aluminum alloy brazing sheet
JP5532520B2 (ja) * 2010-09-29 2014-06-25 日本軽金属株式会社 アルミニウム合金部材の面ろう付け方法

Patent Citations (10)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
JPH036355A (ja) * 1989-05-31 1991-01-11 Showa Alum Corp 無電解Ｚｎメッキ用アルミニウム材の製造方法
JP2001262264A (ja) * 2000-03-21 2001-09-26 Kobe Steel Ltd 靱性および曲げ性に優れたＡｌ−Ｍｇ−Ｓｉ系Ａｌ合金板
JP2004332106A (ja) * 2003-04-15 2004-11-25 Nippon Light Metal Co Ltd プレス成形性および連続抵抗スポット溶接性に優れたアルミニウム合金板およびその製造方法
JP2008308760A (ja) 2006-12-21 2008-12-25 Mitsubishi Alum Co Ltd ろう付によって製造される高強度自動車熱交換器用部材に用いられる、成形性と耐エロージョン性に優れた自動車熱交換器用高強度アルミニウム合金材、及びその製造方法
JP2008303405A (ja) 2007-06-05 2008-12-18 Mitsubishi Alum Co Ltd 熱交換器ヘッダプレート用アルミニウム合金材料および熱交換器用ろう付け体
JP2009068056A (ja) * 2007-09-12 2009-04-02 Sumitomo Light Metal Ind Ltd レーザ溶接性に優れたアルミニウム合金板材
JP2009161835A (ja) 2008-01-09 2009-07-23 Sumitomo Light Metal Ind Ltd アルミニウム製熱交換器及びその製造方法
JP2010168613A (ja) 2009-01-21 2010-08-05 Furukawa-Sky Aluminum Corp 熱交換器用単層ブレージングシートおよびそれを使用した熱交換器
JP2012040611A (ja) * 2010-07-20 2012-03-01 Furukawa-Sky Aluminum Corp アルミニウム合金材を用い、耐食性に優れた構造体とその接合方法
JP2012051028A (ja) * 2010-08-06 2012-03-15 Furukawa-Sky Aluminum Corp アルミニウム合金材を用いた構造体とその接合方法

Non-Patent Citations (2)

* Cited by examiner, † Cited by third party
Title
"Aluminum Brazing Handbook (revised edition", 2003, JAPAN LIGHT METAL WELDING & CONSTRUCTION ASSOCIATION
See also references of EP2787094A4

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WO2014184880A1 (fr) * 2013-05-14 2014-11-20 株式会社Uacj Matériau d'alliage d'aluminium, dont une couche unique permet une fixation thermique ; procédé de fabrication de celui-ci ; et corps fixé en aluminium utilisant ledit matériau d'alliage d'aluminium
WO2014196183A1 (fr) * 2013-06-02 2014-12-11 株式会社Uacj Échangeur thermique et matériau d'ailette pour ledit échangeur thermique
US10408550B2 (en) 2013-06-02 2019-09-10 Uacj Corporation Heat exchanger, and fin material for said heat exchanger
CN103796347A (zh) * 2014-03-03 2014-05-14 南通华特铝热传输材料有限公司 用于家用空调ptc发热器的复合铝条
CN104697383A (zh) * 2015-03-31 2015-06-10 东莞市闻誉实业有限公司 散热板
CN104697383B (zh) * 2015-03-31 2016-10-05 东莞市闻誉实业有限公司 散热板
CN114423563A (zh) * 2019-10-04 2022-04-29 三菱铝株式会社 铝钎焊片材和铝部件的无助焊剂钎焊方法
CN114423563B (zh) * 2019-10-04 2022-12-06 Ma铝株式会社 铝钎焊片材和铝部件的无助焊剂钎焊方法
WO2022138171A1 (fr) * 2020-12-23 2022-06-30 株式会社Uacj Échangeur de chaleur, matériau de tube d'échangeur de chaleur et matériau d'ailette d'échangeur de chaleur
CN112743304A (zh) * 2020-12-30 2021-05-04 深圳市恩利来科技有限公司 一种环保合金材料精深加工方法
WO2022176420A1 (fr) * 2021-02-16 2022-08-25 株式会社Uacj Tôle en alliage d'aluminium et son procédé de production, et échangeur de chaleur

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US9903008B2 (en) 2018-02-27
BR112014013132B1 (pt) 2022-05-31
US20150050520A1 (en) 2015-02-19
CN103930577A (zh) 2014-07-16
JP2013249540A (ja) 2013-12-12
US9574253B2 (en) 2017-02-21
IN2014MN01031A (fr) 2015-05-01
PL2787094T3 (pl) 2017-06-30
US20170137919A1 (en) 2017-05-18
ES2613590T3 (es) 2017-05-24
EP2787094A4 (fr) 2015-12-09
JPWO2013080650A1 (ja) 2015-04-27
KR20140099312A (ko) 2014-08-11
EP2787094B1 (fr) 2016-12-07
EP2787094A1 (fr) 2014-10-08
CN103930577B (zh) 2015-05-20
KR101581607B1 (ko) 2015-12-30
BR112014013132A2 (pt) 2018-08-21
JP5337326B1 (ja) 2013-11-06
JP5436714B2 (ja) 2014-03-05

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